High-strength, soft-magnetic iron-cobalt-vanadium alloy

ABSTRACT

A high-strength, soft-magnetic iron-cobalt-vanadium alloy selection is proposed, consisting of 35.0≦Co≦55.0% by weight, 0.75≦V≦2.5% by weight, O≦Ta+2×Nb≦0.8% by weight, 0.3&lt;Zr≦1.5% by weight, remainder Fe and melting-related and/or incidental impurities. This zirconium-containing alloy selection has excellent mechanical properties, in particular a very high yield strength, high inductances and particularly low coercive forces. It is eminently suitable for use as a material for magnetic bearings used in the aircraft industry.

This application claims foreign priority to German application number DE10320350.8 filed May 7, 2003.

TECHNICAL FIELD OF THE INVENTION

The invention relates to a high-strength, soft-magnetic iron-cobalt-vanadium alloy which can be used in particular for electrical generators, motors and magnetic bearings in aircraft. Electric generators, motors and magnetic bearings in aircraft, in addition to a small overall size, must also have the minimum possible weight. Therefore, soft-magnetic iron-cobalt-vanadium alloys which have a high saturation induction are used for these applications.

BACKGROUND OF THE INVENTION

The binary iron-cobalt alloys with a cobalt content of between 33 and 55% by weight are extraordinarily brittle, which is attributable to the formation of an ordered superstructure at temperatures below 730° C. The addition of approximately 2% by weight of vanadium impedes the transition to this superstructure, so that relatively good cold workability can be achieved after quenching to room temperature from temperatures of over 730° C.

Accordingly, a known ternary base alloy is an iron-cobalt-vanadium alloy which contains 49% by weight of iron, 49% by weight of cobalt and 2% by weight of vanadium. This alloy has long been known and is described extensively, for example, in “R. M. Bozorth, Ferromagnetism, van Nostrand, New York (1951)”. This vanadium-containing iron-cobalt alloy is distinguished by its very high saturation induction of approx. 2.4 T.

A further development of this ternary vanadium-containing cobalt-iron base alloy is known from U.S. Pat. No. 3,634,072, which describes, during the production of alloy strips, quenching of the hot-rolled alloy strip from a temperature above the phase transition temperature of 730° C. This process is required in order to make the alloy sufficiently ductile for the subsequent cold rolling. The quenching suppresses the ordering. In manufacturing terms, however, the quenching is highly critical, since what are known as the cold-rolling passes can very easily cause fractures in the strips. Therefore, considerable efforts have been made to increase the ductility of the alloy strips and thereby to increase manufacturing reliability.

Therefore, U.S. Pat. No. 3,634,072 proposes, as ductility-increasing additives, the addition of 0.02 to 0.5% by weight of niobium and/or 0.07 to 0.3% by weight of zirconium.

Niobium, which incidentally may also be replaced by the homologous element tantalum, in the iron-cobalt alloying system, not only has the property of greatly reducing the degree of order, as has been described, for example, by R. V. Major and C. M. Orrock in “High saturation ternary cobalt-iron based alloys”, IEEE Trans. Magn. 24 (1988), 1856-1858, but also inhibits grain growth.

The addition of zirconium in the quantity of at most 0.3% by weight proposed by U.S. Pat. No. 3,634,072 likewise inhibits grain growth. Both mechanisms significantly improve the ductility of the alloy after quenching.

In addition to this high-strength niobium- and zirconium-containing iron-cobalt-vanadium alloy which is known from U.S. Pat. No. 3,634,072, zirconium-free alloys are also known, from U.S. Pat. No. 5,501,747.

That document proposes iron-cobalt-vanadium alloys which are used in fast aircraft generators and magnetic bearings. U.S. Pat. No. 5,501,747 is based on the teaching of U.S. Pat. No. 3,364,072 and restricts the niobium content disclosed therein to 0.15-0.5% by weight. Furthermore, U.S. Pat. No. 5,501,747 recommends a special magnetic final anneal, in which the alloy can be heat-treated for no more than approximately four hours, preferably no more than two hours, at a temperature of no greater than 740° C., in order to produce an object which has a yield strength of at least approximately 620 MPa. This is very limiting and also very unusual, since the soft-magnetic iron-cobalt-vanadium alloys are normally annealed at temperatures of over 740° C. and below 900° C.

The magnetic and mechanical properties can be adjusted by means of the annealing temperature. Both properties are crucial for use of the alloys. However, it is very difficult to simultaneously optimize these two properties, since the properties are contradictory:

1. If the alloy is annealed at a relatively high temperature, the result is a coarser grain and therefore good soft-magnetic properties. However, the mechanical properties obtained are generally relatively poor.

2. On the other hand, if the alloy is annealed at lower temperatures, better mechanical properties are obtained, on account of a finer grain, but the finer grain results in worse magnetic properties.

A major drawback of the alloy selection disclosed by U.S. Pat. No. 5,501,747 is the need for the abovementioned rapid anneal, which may only be carried out for approximately one to two hours at a temperature close to the ordered/unordered phase boundary in order to achieve usable magnetic and mechanical properties.

If there is a very large quantity of material to be annealed, reliable production can therefore only be realized with very great difficulty, on account of different heat-up times and on account of temperature fluctuations within the material to be annealed. On a large industrial scale, the result is generally unacceptable scatters with regard to the yield strengths which are characteristic of the mechanical properties.

SUMMARY OF THE INVENTION

Therefore, it is an object of the present invention to provide a new high-strength, soft-magnetic iron-cobalt-vanadium alloy selection which is distinguished by very good mechanical properties, in particular by very high yield strengths.

Furthermore, the alloys should have yield strengths of over 600 MPa, preferably of over 700 MPa, even with longer annealing times of at least two hours and with a high manufacturing reliability.

Furthermore, the alloys should at the same time have high saturation inductances and the lowest possible coercive forces, i.e. should have excellent soft-magnetic properties.

According to the invention, this object is achieved by a soft-magnetic iron-cobalt-vanadium alloy selection which substantially comprises

-   35.0≦Co≦55.0% by weight, -   0.75≦V≦2.5% by weight, -   0≦(Ta+2×Nb)≦0.8% by weight, -   0.3<Zr≦1.5% by weight, -   Ni≦5.0% by weight, -   remainder Fe and melting-related and/or incidental impurities.

In this context and in the text which follows, the term “substantially comprises” is to be understood as meaning that the alloy selection according to the invention, in addition to the main constituents indicated, namely Co, V, Zr, Nb, Ta and Fe, may only include melting-related and/or incidental impurities in a quantity which has no significant adverse effect on either the mechanical properties or the magnetic properties.

Entirely surprisingly, it has emerged that iron-cobalt-vanadium alloys with zirconium contents of over 0.3% by weight have significantly better mechanical properties, while at the same time achieving excellent magnetic properties, than the prior art alloys described in the introduction.

This can be attributed to the fact that, on account of the addition of zirconium in quantities greater than 0.3% by weight, a previously unknown hexagonal Laves phase is formed within the microstructure between the individual grains, and this has a very positive effect on the mechanical and magnetic properties. This hexagonal Laves phase should not be confused, in terms of its metallurgy and crystallography, with the cubic Laves phase described in U.S. Pat. No. 5,501,747. Only the name is partially identical. This significant addition of zirconium results in a significant improvement in ductility, in particular when used in conjunction with niobium and/or tantalum.

BRIEF DESCRIPTION OF THE DRAWINGS

In the text which follows, comparative examples and exemplary embodiments of the present invention are explained in detail with reference to Tables 1 to 33 and FIGS. 1 to 15, in which:

-   -   Table 1 shows properties of special melts from batches 93/5964         to 93/6018 after final annealing for one hour at 720° C. under         H₂;     -   Table 2 shows properties of special melts from batches 93/6278         to 93/6289 after final annealing for one hour at 720° C. under         H₂;     -   Table 3 shows properties of special melts from batches 93/6655         to 93/6666 after final annealing for one hour at 720° C. under         H₂;     -   Table 4 shows properties of special melts from batches 93/5964         to 93/6018 after final annealing for two hours at 720° C. under         H₂;     -   Table 5 shows properties of special melts from batches 93/6278         to 93/6289 after final annealing for two hours at 720° C. under         H₂;     -   Table 6 shows properties of special melts from batches 93/6655         to 93/6666 after final annealing for two hours at 720° C. under         H₂;     -   Table 7 shows properties of special melts from batches 93/6278         to 93/6289 after final annealing for four hours at 720° C. under         H₂;     -   Table 8 shows properties of special melts from batches 93/6655         to 93/6666 after final annealing for four hours at 720° C. under         H₂;     -   Table 9 shows properties of special melts from batches 93/6278         to 93/6289 after final annealing for one hour at 730° C. under         H₂;     -   Table 10 shows properties of special melts from batches 93/6278         to 93/6289 after final annealing for two hours at 730° C. under         H₂;     -   Table 11 shows properties of special melts from batches 93/6278         to 93/6289 after final annealing for one hour at 740° C. under         H₂;     -   Table 12 shows properties of special melts from batches 93/6655         to 93/6666 after final annealing for one hour at 740° C. under         H₂;     -   Table 13 shows properties of special melts from batches 93/6278         to 93/6289 after final annealing for two hours at 740° C. under         H₂;     -   Table 14 shows properties of special melts from batches 93/6655         to 93/6666 after final annealing for two hours at 740° C. under         H₂;     -   Table 15 shows properties of special melts from batches 93/5964         to 93/6018 after final annealing for four hours at 740° C. under         H₂;     -   Table 16 shows properties of special melts from batches 93/6278         to 93/6306 after final annealing for four hours at 740° C. under         H₂;     -   Table 17 shows properties of special melts from batches 93/6655         to 93/6666 after final annealing for four hours at 740° C. under         H₂;     -   Table 18 shows properties of special melts from batches 93/6278         to 93/6289 after final annealing for one hour at 750° C. under         H₂;     -   Table 19 shows properties of special melts from batches 93/6278         to 93/6289 after final annealing for one hour at 770° C. under         H₂;     -   Table 20 shows properties of special melts from batches 93/6278         to 93/6289 after final annealing for two hours at 770° C. under         H₂;     -   Table 21 shows properties of special melts from batches 93/5964         to 93/6018 after final annealing for four hours at 770° C. under         H₂;     -   Table 22 shows properties of special melts from batches 93/6278         to 93/6284 after final annealing for four hours at 770° C. under         H₂;     -   Table 23 shows properties of special melts from batches 93/6655         to 93/6666 after final annealing for four hours at 770° C. under         H₂;     -   Table 24 shows properties of special melts from batches 93/5964         to 93/6018 after final annealing for four hours at 800° C. under         H₂;     -   Table 25 shows properties of special melts from batches 93/6278         to 93/6306 after final annealing for four hours at 800° C. under         H₂;     -   Table 26 shows properties of special melts from batches 93/6655         to 93/6666 after final annealing for four hours at 800° C. under         H₂;     -   Table 27 shows the microstructural state of special melts         93/7179 to 93/7183 after quenching from various temperatures;     -   Table 28 shows properties of batches 93/7180 to 93/7184 and         74/5517 and 99/5278 after final annealing for one hour at         720° C. under H₂, thickness: 0.35 mm;     -   Table 29 shows hysteresis losses for special melts from batches         93/7180 to 93/7184 and 74/5517 and 99/5278 for various degrees         of saturation and frequencies after final annealing for one hour         at 720° C. under H₂, thickness 0.35 mm;     -   Table 30 shows properties of batches 93/7180 to 93/7184 and         74/5517 and 99/5278 after final annealing for two hours at         750° C. under H₂, thickness: 0.35 mm;     -   Table 31 shows hysteresis losses for special melts from batches         93/7180 to 93/7184 and 74/5517 and 99/5278 for various degrees         of saturation and frequencies after final annealing for two         hours at 750° C. under H₂, thickness 0.35 mm;     -   Table 32 shows properties of batches 93/7180 to 93/7184 and         74/5517 and 99/5278 after final annealing for four hours at         840° C. under H₂, thickness: 0.35 mm;     -   Table 33 shows hysteresis losses for special melts from batches         93/7180 to 93/7184 and 74/5517 and 99/5278 for various degrees         of saturation and frequencies after final annealing for four         hours at 840° C. under H₂, thickness: 0.35 mm;

FIG. 1 is a graph summarizing properties of a prior art alloy 93/5968 (Masteller);

FIG. 2 is a graph summarizing properties of a prior art alloy 93/5969 (Masteller);

FIG. 3 is a graph summarizing properties of a prior art alloy 93/5973 (Ackermann);

FIG. 4 is a graph summarizing properties of an exemplary alloy 93/6279 of the present invention;

FIG. 5 is a graph summarizing properties of an exemplary alloy 93/6284 of the present invention;

FIG. 6 is a graph summarizing properties of an exemplary alloy 93/6285 of the present invention;

FIG. 7 is a graph summarizing properties of an exemplary alloy 93/6655 of the present invention;

FIG. 8 is a graph summarizing properties of an exemplary alloy 93/6661 of the present invention;

FIGS. 9-11 show the relationship between induction and field strength for exemplary embodiments of the alloy of the present invention 93/7180 to 93/7184;

FIGS. 12-13 show the relationship between Co content and V content and yield strength R_(p0.2); and

FIGS. 14-15 show the relationship between resistivity ρ_(e1) and Co and V content for various annealing parameters.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS OF THE INVENTION

In a preferred embodiment, the soft-magnetic iron-cobalt-vanadium alloy according to the invention has a zirconium content of 0.5≦Zr≦1.0% by weight, ideally a zirconium content of 0.6≦Zr≦0.8% by weight.

The cobalt content is typically 48.0≦Co≦50.0% by weight. However, very good results can also be achieved with alloys with a cobalt content of between 45.0≦Co≦48.0% by weight. The nickel content should be Ni≦1.0% by weight, ideally Ni≦0.5% by weight.

In one typical configuration of the present invention, the soft-magnetic iron-cobalt-vanadium alloy according to the invention has a vanadium content of 1.0≦V≦2.0% by weight, ideally a vanadium content of 1.5≦V≦2.0% by weight.

To achieve particularly good ductilities, the present invention provides for niobium and/or tantalum contents of 0.04≦(Ta+2×Nb)≦0.8% by weight, ideally of 0.04≦(Ta+2×Nb)≦0.3% by weight.

The soft-magnetic high-strength iron-cobalt-vanadium alloys according to the invention also have a content of melting-related and/or incidental metallic impurities of:

-   Cu≦0.2, Cr≦0.3, Mo≦0.3, Si≦0.5, Mn≦0.3 and Al≦0.3; preferably of: -   Cu≦0.1, Cr≦0.2, Mo≦0.2, Si≦0.2, Mn≦0.2 and Al≦0.2; ideally of: -   Cu≦0.06, Cr≦0.1, Mo≦0.1, Si≦0.1 and Mn≦0.1.

Furthermore, nonmetallic impurities are typically present in the following ranges:

-   P≦0.01, S≦0.02, N≦0.005, O≦0.05 and C≦0.05; preferably in the     following ranges: -   P≦0.005, S≦0.01, N≦0.002, O≦0.02 and C≦0.02; ideally in the     following ranges: -   S≦0.005, N≦0.001, O≦0.01 and C≦0.01.

The alloys according to the invention can be melted by means of various processes. In principle, all conventional techniques, such as for example melting in air or production by vacuum induction melting (VIM), are possible.

However, the VIM process is preferred for production of the soft-magnetic iron-cobalt-vanadium alloys according to the invention, since the relatively high zirconium contents can be set more successfully. In the case of melting in air, zirconium-containing alloys have high melting losses, with the result that undesirable zirconium oxides and other impurities are formed. Overall, the zirconium content can be set more successfully if the VIM process is used.

The alloy melt is then cast into chill molds. After solidification, the ingot is desurfaced and then rolled into a slab at a temperature of between 900° C. and 1300° C.

As an alternative, it is also possible to do without the step of desurfacing the oxide skin on the surface of the ingots. Instead, the slab then has to be machined accordingly at its surface.

The resulting slab is then hot-rolled at similar temperatures, i.e. at temperatures above 900° C., to a strip. The hot-rolled alloy strip then obtained is too brittle for a further cold-rolling process. Accordingly, the hot-rolled alloy strip is quenched from a temperature above the ordered/unordered phase transition, which is known to be a temperature of approximately 730° C., in water, preferably in iced brine.

This treatment makes the alloy strip sufficiently ductile. After the oxide skin on the alloy strip has been removed, for example by pickling or blasting, the alloy strip is cold-rolled, for example to a thickness of approximately 0.35 mm.

Then, the desired shapes are produced from the cold-rolled alloy strip. This shaping operation is generally carried out by punching. Further processes include laser cutting, EDM, water jet cutting or the like.

After this treatment, the important magnetic final anneal is carried out, it being possible to precisely set the magnetic properties and mechanical properties of the end product by varying the annealing time and the annealing temperature.

The invention is explained below on the basis of exemplary embodiments and comparative examples. The differences between the individual alloys in terms of their mechanical and magnetic properties are explained with reference to FIGS. 1 to 8, which each show the coercive force H_(c) as a function of the yield strength R_(p0.2).

All the exemplary embodiments and all the comparative examples were produced by casting melts into flat chill molds under vacuum. The oxide skin present on the ingots was then removed by milling.

Then, the ingots were hot-rolled at a temperature of 1150° C. together with a thickness of d=3.5 mm.

The resulting slabs were then quenched in ice water from a temperature T=930° C. The quenched, hot-rolled slabs were finally cold-rolled to a thickness d′=0.35 mm. Then, tensile specimens and rings were punched out. The respective magnetic final anneals were carried out on the rings and tensile specimens obtained.

All the alloy parameters, magnetic measurement results and mechanical measurement results are reproduced in Tables 1 to 26.

To investigate the mechanical properties, tensile tests were carried out, in which the modulus of elasticity E, the yield strength R_(p0.2), the tensile strength R_(m), the elongation at break A_(L) and the hardness HV were measured. The yield strength R_(p0.2) was considered the most important mechanical parameter in this context.

The magnetic properties were tested on the punched rings. The static B-H initial magnetization curve and the static coercive force H_(c) of the punched rings were determined.

COMPARATIVE EXAMPLES

Alloy in accordance with the prior art were produced under designations batches 93/5973 and under designations batch 93/5969 and 93/5968. Batch 93/5973 corresponds to an alloy as described in U.S. Pat. No. 3,634,072 (Ackermann), as cited in the introduction, i.e. a high-strength, soft-magnetic iron-cobalt-vanadium alloy with a low level of added zirconium of less than 0.3% by weight.

The precise amount of zirconium added was 0.28% by weight.

Batches 93/5969 and 93/5968 were alloys corresponding to U.S. Pat. No. 5,501,747 (Masteller), cited in the introduction. These were high-strength, soft-magnetic iron-cobalt-vanadium alloys without any zirconium.

The properties of these alloys are given in Tables 1, 4, 15, 21 and 24. These tables reproduce the properties of the molten alloys with various final anneals. The duration of the final anneals and the annealing temperatures were varied. The annealing temperatures were varied from 720° C. to 800° C. The duration of the final anneals was varied from one hour to four hours.

A graph summarizing the results found for these three alloys from the prior art is given in FIGS. 1, 2 and 3. As can be seen from these figures, with these alloys a high yield strength, i.e., a yield strength R_(p0.2) of over 700 MPa, can only be achieved if significant losses in the soft-magnetic properties are accepted. All three alloys have a semihard-magnetic behavior, i.e. a coercive force H_(c) of more than 6.0 A/cm, in the range of 700 MPa and above.

Exemplary Embodiments:

As exemplary embodiments according to the present invention, five different alloy batches were produced, listed under batch designations 93/6279, 93/6284, 93/6285, 93/6655 and 93/6661 in Tables 2, 3, 5, 6, 7, 8, 9, 10, 11, 12, 13, 14, 16, 17, 22, 23, 25 and 26.

In these alloys, firstly the zirconium content was varied, and secondly the zirconium content together with the other alloying constituents niobium and tantalum that are responsible for the ductility were varied.

With these alloy batches too, both the annealing temperatures for the magnetic final anneals and the final annealing times were varied. The final annealing times were varied between one hour and four hours. The final annealing temperatures were varied between 720° and 800° C.

A graph summarizing the individual results is given in FIGS. 4 to 8. These figures also show the coercive force H_(c) as a function of the yield strength R_(p0.2). Unlike with the alloys from the prior art, which have been discussed above under the Comparative Examples, the alloys according to the present invention have very high yield strengths combined, at the same time, with very good soft-magnetic properties.

This can be seen in particular from FIGS. 7 and 8. The alloys shown there have yield strengths of over 700 MPa combined with coercive forces of approximately 5.0 A/cm.

It can be seen in particular from FIG. 3 that if zirconium contents of less than 0.30% by weight are used, as disclosed by U.S. Pat. No. 3,634,072, it is not in fact possible to produce truly high-strength alloys.

By comparison with the composition 49.2 Co; 1.9 V; 0.16 Ta; 0.77 Zr; remainder Fe, the V content was varied from 0-3% and the Co content from 10-49% in batches 93/7179 to 93/7184. These exemplary embodiments are compiled in FIGS. 9 to 15 and Tables 26 to 32. Batch 74/5517 99/5278 is a comparison alloy from the prior art.

Table 26 shows the investigation into the appropriate quenching temperature for the special melt tests of batches 93/7179 to 93/7183. Only batch 93/7184 was cold-rolled without quenching. After quenching at the temperatures determined in each instance, cf. Table 26, it was possible for the strips to be cold-rolled to their final thickness.

FIGS. 9 to 11 show the relationship between induction and field strength for batches 93/7180 to 93/7184 after a final anneal under various annealing parameters. Inductances are corrected for air flow in accordance with ASTM A 341/A 341M and IEC 404-4. These results and the results of the tensile tests are listed in Tables 27, 29 and 31.

The relationship between Co content and V content and yield strength R_(p0.2) is illustrated in graph form in FIGS. 12 and 13.

Tables 28, 30 and 32 show the resistivity and the hysteresis losses for batches 93/7179 to 93/7184. The relationship between resistivity ρ_(e1) and Co and V content for various annealing parameters is presented in graph form in FIGS. 14 and 15.

The alloys according to the present invention are particularly suitable for magnetic bearings, in particular for the rotors of magnetic bearings, as described in U.S. Pat. No. 5,501,747, and as material for generators and for motors. TABLE 1 Strip 0.35 mm  1 h 720° C., H2, OK Static magnetic measurements Wt. % H_(c) B₈ ¹⁾ B₁₆ ¹⁾ B₂₄ ¹⁾ Batch Co V Nb Ni Addition [A/cm] B₃ ¹⁾ [T] [T] [T] [T] 93/5973 49.10 1.95 0.03 Zr˜0.28 10.945 0.088 0.368 1.669 1.893 93/5969 49.10 1.91 0.37 0.04 10.638 0.087 0.394 1.861 1.985 93/5968 49.10 1.91 0.23 0.04 12.144 0.077 0.287 1.650 1.918 Without air flow Mechanical correction from B₄₀ measurements B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ R_(m) R_(p0.2) A_(L) E-Modulus Batch [T] [T] [T] [MPa] [MPa] [%] [GPa] HV 93/5973 2.018 2.135 2.222 1229 721 11.8-16.6 219-262 371-377 93/5969 2.080 2.180 2.270 1521 939 19.2-21.2 251-264 421-432 93/5968 2.038 2.152 2.246 1498 890 21.3-21.8 239-271 414-418

TABLE 2 Anneal: 1 h, 720° C., H2, OK Wt. % Static magnetic measurements Mechanical measurements Ad- H_(c) B₃ R_(m) R_(p0.2) A_(L) E-Modulus Batch Co V Ni dition (A/cm) (T) B₈ (T) B₁₆ (T) B₂₄ (T) (MPa) (MPa) (%) (GPa) HV5 93/6279 49.20 1.89 0.06 Zr˜0.80 2.815 0.549 1.902 2.054 2.115 970 633 8.5 241 312 93/6284 49.35 1.90 0.43 Zr˜1.00 3.435 0.319 1.798 1.995 2.066 993 663 7.6-9.5 235 329 93/6285 49.35 1.89 0.44 Zr˜1.40 3.381 0.334 1.797 1.983 2.061 953 675 6.9-8.3 243 333

TABLE 3 Anneal: 1 h/720° C./H2/OK/    With air flow correction from B₄₀ Mechanical measurements Wt. % H_(c) B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ Batch Co V Nb Zr Ta (A/cm) (T) (T) (T) (T) (T) (T) (T) 93/6655 49.15 1.90 0.10 # 0.86 x 5.265 0.204 1.393 1.850 1.965 2.050 2.130 2.170 93/6661 49.70 1.91 x # 0.77 # 0.16 6.397 0.175 1.121 1.824 1.945 2.037 2.118 2.170 Mechanical measurements R_(m) R_(p0.2) A_(L) E-Modulus Batch (MPa) (MPa) (%) (GPa) HV 93/6655 1101-1251 753-772  9.7-13.9 239-248 326-332 93/6661 1245-1285 831-833 12.3-14.7 223-251 341-349 ¹⁾Induction B at a field H in A/cm, e.g. B₂₄ at H = 24 A/cm

TABLE 4 Strip 0.35 mm  2 h 720° C., H2, OK Static magnetic measurements Wt. % H_(c) B₈ ¹⁾ B₁₆ ¹⁾ B₂₄ ¹⁾ Batch Co V Nb Ni Addition [A/cm] B₃ ¹⁾ [T] [T] [T] [T] 93/5973 49.10 1.95 0.03 Zr˜0.28 1.810 1.687 2.028 2.141 2.189 93/5969 49.10 1.91 0.37 0.04 6.442 0.161 1.384 1.990 2.068 93/5968 49.10 1.91 0.23 0.04 5.791 0.183 1.499 1.986 2.066 Without air flow Mechanical correction from B₄₀ measurements B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ R_(m) R_(p0.2) A_(L) E-Modulus Batch [T] [T] [T] [MPa] [MPa] [%] [GPa] HV 93/5973 2.236 2.303 2.378  907 504 9.5-9.6 246-263 247-261 93/5969 2.151 2.239 2.316 1379 761 15.1-22.5 257-268 332-335 93/5968 2.146 2.232 2.307 1335 700 16.6-23.0 243-250 323-326

TABLE 5 Anneal: 2 h, 720° C., H₂, OK Mechanical measurements Wt. % Static magnetic measurements R_(m) R_(p0.2) A_(L) E-Modulus Batch Co V Ni Addition H_(c) (A/cm) B₃ (T) B₈ (T) B₁₆ (T) B₂₄ (T) (MPa) (MPa) (%) (GPa) HV5 93/6279 49.20 1.89 0.06 Zr˜0.80 3.172 0.417 1.836 2.024 2.092 1041 612 9.7-11.0 242-243 283-293 93/6284 49.35 1.90 0.43 Zr˜1.00 2.950 0.588 1.843 2.010 2.084 965 636 5.1-11.3 245-247 291-294 93/6285 49.35 1.89 0.44 Zr˜1.40 3.287 0.412 1.847 1.969 2.048 1060 641 8.0-11.3 246-247 300-304

TABLE 6 Anneal: 2 h/720° C./H2/OK/    With air flow correction from B₄₀ magnetic measurements Wt. % H_(c) B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ Batch Co V Nb Zr Ta (A/cm) (T) (T) (T) (T) (T) (T) (T) 93/6655 49.15 1.90 0.10 # 0.86 x 4.003 0.295 1.630 1.922 2.017 2.092 2.161 2.205 93/6661 49.70 1.91 x # 0.77 # 0.16 5.218 0.218 1.429 1.887 1.991 2.068 2.145 2.196 Mechanical measurements R_(m) R_(p0.2) A_(L) E-Modulus Batch (MPa) (MPa) (%) (GPa) HV 93/6655 1095-1187 679-695 10.3-12.8 247-253 309-312 93/6661 1100-1267 749-766  9.3-13.9 235-249 323-329 ¹⁾Induction B at a field H in A/cm, z.B. B₂₄ at H = 24 A/cm

TABLE 7 Anneal: 4 h, 720° C., H2, OK magnetic measurements With air flow p_(Fe) ²⁾ p_(Fe) ²⁾ correction from B₄₀ Wt. % H_(c) p_(hyst)/f f = 400 Hz f = 1000 Hz B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ Batch Co V Ni Addition (A/cm) (J/kg) (W/kg) (W/kg) (T) (T) (T) 93/6279 49.20 1.89 0.06 Zr˜0.80 1.600 0.1214  91.302 388.531 1.781 2.016 2.117 93/6284 49.35 1.90 0.43 Zr˜1.00 1.949 0.1502 100.746 404.399 1.629 1.958 2.075 93/6285 49.35 1.89 0.44 Zr˜1.40 2.005 1.606 1.959 2.070 With air flow correction from B₄₀ Mechanical measurements B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ R_(m) R_(p0.2) A_(L) E-Modulus Batch (T) (T) (T) (T) (MPa) (MPa) (%) (GPa) HV5 93/6279 2.158 2.187 2.219 2.248 849 510 5.8-9.4 228-233 282-302 93/6284 2.127 2.163 2.198 2.227 940 558 7.1-9.2 236-254 319-321 93/6285 2.121 913 570 6.8-8.2 230-238 336-338 p_(hyst)/f: static Hysteresis losses at B = 2 T ¹⁾Induction B at a field H in A/cm, e.g. B₄₀ at H = 40 A/cm ²⁾P_(Fe) at B = 2 T

TABLE 8 Anneal: 4 h/720° C./H2/OK    With air flow correction from B₄₀ magnetic measurements p_(Fe) ²⁾ p_(Fe) ²⁾ Wt. % H_(c) p_(hyst)/f f = 400 Hz f = 1000 Hz B₃ ¹⁾ B₈ ¹⁾ Batch Co V Nb Zr Ta (A/cm) (J/kg) (W/kg) (W/kg) (T) (T) 93/6655 49.15 1.90 0.10 # 0.86 x 3.038 0.2482 139.757 501.111 0.602 1.738 93/6661 49.70 1.91 x # 0.77 # 0.16 3.913 0.3098 164.061 560.637 0.320 1.680 Mechanical measurements magnetic measurements E- B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ R_(m) R_(p0.2) A_(L) Modulus Batch (T) (T) (T) (T) (T) (MPa) (MPa) (%) (GPa) HV 93/6655 1.959 2.044 2.110 2.170 2.207 1107-1119 622-624 11.3-11.4 234-243 277-292 93/6661 1.952 2.035 2.035 2.165 2.206 1167-1241 692-700 11.7-13.9 240-250 310-329 p_(hyst)/f: static Hysteresis losses at B = 2 T ¹⁾Induction B at a field H in A/cm, e.g. B₂₄ at H = 24 A/cm ²⁾p_(Fe) at B = 2 T

TABLE 9 Anneal: 1 h, 730° C., H2, OK Wt. % Static magnetic measurements Mechanical measurements Ad- H_(c) B₃ B₈ R_(m) R_(p0.2) A_(L) E-Modulus Batch Co V Ni dition (A/cm) (T) (T) B₁₆ (T) B₂₄ (T) (MPa) (MPa) (%) (GPa) HV5 93/6279 49.20 1.89 0.06 Zr˜0.80 1.966 1.687 1.999 2.104 2.155 938 583 8.4-8.6 243-244 280-281 93/6284 49.35 1.90 0.43 Zr˜1.00 2.514 0.929 1.921 2.056 2.114 997 611 9.1-9.3 243-249 300 93/6285 49.35 1.89 0.44 Zr˜1.40 2.431 1.125 1.913 2.045 2.103 964 629 6.5-9.4 237-250 301-303

TABLE 10 Anneal: 2 h, 730° C., H2, OK Wt. % Static magnetic measurements Mechanical measurements Ad- H_(c) R_(m) R_(p0.2) A_(L) E-Modulus Batch Co V Ni dition (A/cm) B₃ (T) B₈ (T) B₁₆ (T) B₂₄ (T) (MPa) (MPa) (%) (GPa) HV5 93/6279 49.20 1.89 0.06 Zr˜0.80 1.717 1.758 2.017 2.118 2.169 875 513 7.3-9.0 238 270 93/6284 49.35 1.90 0.43 Zr˜1.00 2.115 1.515 1.962 2.083 2.133 884 547 6.0-8.9 236 285 93/6285 49.35 1.89 0.44 Zr˜1.40 2.334 1.271 1.921 2.045 2.097 738 561 2.9-7.3 242 297

TABLE 11 Annneal: 1 h 740° C., H2, OK Mechanical measurements Wt. % Static magnetic measurements R_(m) R_(p0.2) A_(L) E-Modulus Batch Co V Ni Addition H_(c) (A/cm) B₃ (T) B₈ (T) B₁₆ (T) B₂₄ (T) (MPa) (MPa) (%) (GPa) HV5 93/6279 49.20 1.89 0.06 Zr˜0.80 1.977 1.600 1.979 2.096 2.152 1051 561 10.2-12.1 230-241 305-314 93/6284 49.35 1.90 0.43 Zr˜1.00 2.282 1.289 1.931 2.066 2.121 1050 605 10.0-10.2 239-242 276-283 93/6285 49.35 1.89 0.44 Zr˜1.40 2.588 0.833 1.874 2.013 2.078 966 612 6.8-9.6 234-236 289-297

TABLE 12 Anneal: 1 h/740° C./H2/OK    With air flow correction from B₄₀ Static magnetic measurements Wt. % H_(c) B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ Batch Co V Nb Zr Ta (A/cm) (T) (T) (T) (T) (T) (T) (T) 93/6655 49.15 1.90 0.10 # 0.86 x 3.203 0.443 1.727 1.954 2.037 2.101 2.161 2.201 93/6661 49.70 1.91 x # 0.77 # 0.16 3.901 0.297 1.699 1.958 2.040 2.105 2.170 2.217 Mechanical measurements R_(m) R_(p0.2) A_(L) E-Modulus Batch (MPa) (MPa) (%) (GPa) HV 93/6655  946-1100 638-650  7.4-11.1 240-241 294-297 93/6661 1169-1173 694-703 12.0-12.3 228-243 303-312 ¹⁾Induction B at a field H in A/cm, e.g. B₂₄ at H = 24 A/cm

TABLE 13 Annneal: 1 h 740° C., H2, OK Mechanical measurements Wt. % Static magnetic measurements R_(m) R_(p0.2) A_(L) E-Modulus Batch Co V Ni Addition H_(c) (A/cm) B₃ (T) B₈ (T) B₁₆ (T) B₂₄ (T) (MPa) (MPa) (%) (GPa) HV5 93/6279 49.20 1.89 0.06 Zr˜0.80 1.646 1.739 1.993 2.095 2.136 922 511  7.2-10.3 237-245 264-272 93/6284 49.35 1.90 0.43 Zr˜1.00 2.073 1.559 1.972 2.088 2.142 886 573 5.6-8.1 234-246 278-284 93/6285 49.35 1.89 0.44 Zr˜1.40 2.100 1.564 1.957 2.076 2.130 967 566 7.9-9.8 234-240 273-288

TABLE 14 Anneal: 2 h/740° C./H2/OK    With air flow correction from B₄₀ Static magnetic measurements Wt. % H_(c) B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ Batch Co V Nb Zr Ta (A/cm) (T) (T) (T) (T) (T) (T) (T) 93/6655 49.15 1.90 0.10 # 0.86 x 2.601 0.776 1.826 2.011 2.082 2.140 2.186 2.217 93/6661 49.70 1.91 x # 0.77 # 0.16 2.773 0.636 1.838 2.012 2.085 2.137 2.189 2.220 Mechanical measurements R_(m) R_(p0.2) A_(L) E-Modulus Batch (MPa) (MPa) (%) (GPa) HV 93/6655 1037-1043 581-592 10.0-10.1 241-243 280-293 93/6661 1127-1143 627-635 11.6-12.5 223-246 289-295 ¹⁾Induction B at a field H in A/cm, z.B. B₂₄ at H = 24 A/cm

TABLE 15 Strip 0.35 mm  4 h 740° C., H2, OK Static magnetic With air flow measurements correction from B₄₀ wt-. % H_(c) B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ Batch Co V Nb Ni Addition [A/cm] [T] [T] [T] [T] [T] [T] [T] 93/5973 49.10 1.95 0.03 Zr˜0.28 1.149 1.931 2.101 2.185 2.219 93/5969 49.10 1.91 0.37 0.04 3.719 0.694 1.838 2.051 2.111 2.172 2.231 2.265 93/5968 49.10 1.91 0.23 0.04 3.194 0.597 1.900 2.078 2.137 2.178 2.230 2.266 Mechanical measurements R_(m) R_(p0.2) A_(L) E-Modulus Batch [MPa] [MPa] [%] [GPa] HV 93/5973 813-874 407-438 8.4-9.7 241-250 231-236 93/5969  930-1261 582-617  8.9-17.5 229-252 275-291 93/5968 1061-1192 569-588 10.9-15.5 245-262 283-295

TABLE 16 Anneal: 4 h, 740° C., H2, OK With air flow Magnetic measurements correction p_(Fe) ²⁾ p_(Fe) ²⁾ from B₄₀ Wt. % H_(c) p_(hyst)/f f = 400 Hz f = 1000 Hz B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ Batch Co V Ni Addition (A/cm) (J/kg) (W/kg) (W/kg) (T) (T) (T) 93/6279 49.20 1.89 0.06 Zr˜0.80 1.456 0.109 85.117 369.182 1.813 2.037 2.132 93/6284 49.35 1.90 0.43 Zr˜1.00 1.690 1.727 2.001 2.104 93/6285 49.35 1.89 0.44 Zr˜1.40 1.974 1.608 1.963 2.073 With air flow correction from B₄₀ Mechanical measurements B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ R_(m) R_(p0.2) A_(L) E-Modulus ρ_(el) Batch (T) (T) (T) (T) (MPa) (MPa) (%) (GPa) HV (Ωmm²/m) 93/6279 2.172 2.199 2.230 2.257 764 484 5.7-6.5 251 242 0.451 93/6284 2.152 830 525 6.2-7.1 250 275 0.449 93/6285 2.121 804 552 3.1-6.8 253 280 0.450

TABLE 17 Anneal: 4 h/740° C./H2/OK/    With air flow correction from B₄₀ magnetic measurements p_(Fe) ²⁾ p_(Fe) ²⁾ Wt. % H_(c) p_(hyst)/f f = 400 Hz f = 1000 Hz B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ Batch Co V Nb Zr Ta (A/cm) (J/kg) (W/kg) (W/kg) (T) (T) (T) 93/6655 49.15 1.90 0.10 # x 2.270 0.1796 113.844 442.061 1.060 1.862 2.031 0.86 93/6661 49.70 1.91 x # # 2.351 0.1856 114.229 435.546 1.031 1.884 2.040 0.77 0.16 magnetic measurements Mechanical measurements B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ R_(m) R_(p0.2) A_(L) E-Modulus Batch (T) (T) (T) (T) (MPa) (MPa) (%) (GPa) HV 93/6655 2.098 2.147 2.190 2.214 1034 538 9.7 255 268-271 93/6661 2.101 2.144 2.193 2.223 1058-1124 572-579 10.6-12.1 231-242 277-281 p_(hyst)/f: static Hysteresis losses at B = 2 T ¹⁾Induction B at a field H in A/cm, z.B. B₂₄ at H = 24 A/cm ²⁾p_(Fe) at B = 2 T

TABLE 18 Anneal: 1 h, 750° C., H2, OK Mechanical measurements wt-% Static magnetic measurements R_(p0.2) E-Modulus Batch Co V Ni Addition H_(c) (A/cm) B₃ (T) B₈ (T) B₁₆ (T) B₂₄ (T) R_(m) (MPa) (MPa) A_(L) (%) (GPa) HV5 93/6279 49.20 1.89 0.06 Zr˜0.80 1.595 1.783 2.033 2.136 2.179 919 533 7.4-9.5 218-250 272-285 93/6284 49.35 1.90 0.43 Zr˜1.00 1.804 1.667 1.965 2.076 2.123 832 547 3.9-8.1 198-223 285-288 93/6285 49.35 1.89 0.44 Zr˜1.40 1.983 1.543 1.921 2.046 2.101 948 572 7.9-8.4 238-256 290-297

TABLE 19 Anneal: 1 h, 770° C., H2, OK Wt-% Static magnetic measurements Mechanical measurements Addi- H_(c) B₃ B₈ R_(m) R_(p0.2) A_(L) E-Modulus Batch Co V Ni tion (A/cm) (T) (T) B₁₆ (T) B₂₄ (T) (MPa) (MPa) (%) (GPa) HV5 93/6279 49.20 1.89 0.06 Zr˜0.80 1.476 1.819 2.028 2.127 2.169 903 486 8.5-9.0 250-252 257-260 93/6284 49.35 1.90 0.43 Zr˜1.00 1.634 1.755 1.997 2.098 2.141 854 511 6.3-8.1 252-265 272-273 93/6285 49.35 1.89 0.44 Zr˜1.40 1.808 1.693 1.961 2.066 2.111 881 528 7.2-8.1 244-264 278-281

TABLE 20 Anneal: 2 h, 770° C., H2, OK Wt-% Static magnetic measurements Mechanical measurements Addi- H_(c) B₃ B₈ R_(m) R_(p0,2) A_(L) E-Modulus Batch Co V Ni tion (A/cm) (T) (T) B₁₆ (T) B₂₄ (T) (MPa) (MPa) (%) (GPa) HV5 93/6279 49.20 1.89 0.06 Zr˜0.80 1.207 1.860 2.035 2.121 2.155 851 421 8.2-9.5 236-244 254-262 93/6284 49.35 1.90 0.43 Zr˜1.00 1.427 1.813 2.014 2.106 2.141 882 451 8.5-9.1 239-244 262-268 93/6285 49.35 1.89 0.44 Zr˜1.40 1.571 1.761 1.977 2.073 2.110 861 486 6.8-7.9 231-249 270-277

TABLE 21 Strip 0.35 mm 4 h 770° C., H2, OK static magnetic Wt-% measurements Addi- B₂₄ ¹⁾ Batch Co V Nb Ni tion H_(c) [A/cm] B₃ ¹⁾ [T] B₈ ¹⁾ [T] B₁₆ ¹⁾ [T] [T] 93/5973 49.10 1.95 0.03 Zr˜0.28 0.885 1.980 2.218 2.200 2.227 93/5969 49.10 1.91 0.37 0.04 2.038 1.582 2.026 2.128 2.174 93/5968 49.10 1.91 0.23 0.04 1.700 1.755 2.061 2.154 2.192 with air flow correction from B₄₀ mechanical measurements B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ R_(m) R_(p0.2) A_(L) E-Modulus Batch [T] [T] [T] [MPa] [MPa] [%] [GPa] HV 93/5973 492-815 370-389 3.6-9.5 232-248 206-210 93/5969 2.211 2.248 2.275 1018-1129 493-501 11.1-13.9 246-250 232-236 93/5968 2.222 2.252 2.275  942-1087 471-479  9.8-13.5 239-253 226-227

TABLE 22 Anneal: 4 h, 770° C., H2, OK Wt-% Magnetic measurements Addi- p_(Fe) ²⁾ f = 400 Hz p_(Fe) ²⁾ f = 1000 Hz Batch Co V Ni tion H_(c) (A/cm) p_(hyst)/f (J/kg) (W/kg) (W/kg) 93/6279 49.20 1.89 0.06 Zr˜0.80 1.234 0.0819 77.873 363.928 93/6284 49.35 1.90 0.43 Zr˜1.00 1.489 0.1241 99.401 442.150 with air flow correction from B₄₀ Mechanical measurements B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ R_(m) R_(p0.2) A_(L) E-Modulus Batch (T) (T) (T) (T) (T) (T) (T) (MPa) (MPa) (%) (GPa) HV 93/6279 1.861 2.062 2.149 2.184 2.207 2.235 2.260 766 444 4.3-7.5 239 250 93/6284 1.608 1.867 1.968 2.010 2.038 2.066 2.090 782 491 4.3-8.0 233 261

TABLE 23 Anneal: 4 h/770° C./H2/OK  with air flow correction from B₄₀ Wt-% Magnetic measurements Batch Co V Nb Zr Ta H_(c) (A/cm) p_(hyst)/f (J/kg) p_(Fe) ²⁾ f = 400 Hz (W/kg) p_(Fe) ²⁾ f = 1000 Hz (W/kg) 93/6655 49.15 1.90 0.10 # x 1.819 0.1445 99.664 418.788 0.86 93/6661 49.70 1.91 x # # 1.586 0.1263 89.614 381.568 0.77 0.16 Magnetic measurements Mechanical measurements B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ R_(m) R_(p0.2) A_(L) E-Modulus Batch (T) (T) (T) (T) (T) (T) (T) (MPa) (MPa) (%) (GPa) HV 93/6655 1.457 1.928 2.067 2.127 2.157 2.194 2.227 856-931 481-484 7.2-8.5 237-241 249-264 93/6661 1.623 1.963 2.085 2.139 2.168 2.208 2.227 940-974 478-485 9.0-9.8 217-225 241-258 p_(hyst)/f: static hysteresis losses B = 2 T ¹⁾Induction B at a field H in A/cm, e.g. B₂₄ at H = 24 A/cm ²⁾P_(Fe) at B = 2 T

TABLE 24 Strip 0.35 mm 4 h 800° C., H2, OK static magnetic measurements Wt-% B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ Batch Co V Nb Ni Addition H_(c) [A/cm] [T] [T] [T] B₂₄ ¹⁾ [T] 93/5973 49.10 1.95 0.03 Zr˜0.28 0.750 2.004 2.141 2.208 2.237 93/5969 49.10 1.91 0.37 0.04 1.548 1.842 2.080 2.157 2.200 93/5968 49.10 1.91 0.23 0.04 1.360 1.902 2.098 2.180 2.216 with air flow correction from B₄₀ mechanical measurements B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ R_(m) R_(p0.2) E-Modulus Batch [T] [T] [T] [MPa] [MPa] A_(L)/% [GPa] HV 93/5973 534-806  365-384 3.7-8.3 233-246 219-228 93/5969 2.226 2.259 2.285 827-1060 446-474  7.2-12.7 235-253 250-258 93/5968 2.235 2.263 2.284 926-1015 435-444 10.2-12.7 245-255 230-234

TABLE 25 Anneal: 4 h, 800° C., H2, OK Magnetic measurements with air flow p_(Fe) ²⁾ p_(Fe) ²⁾ correction Wt-% p_(hyst)/f f = 400 Hz f = 1000 Hz from B₄₀ Batch Co V Ni Addition H_(c) (A/cm) (J/kg) (W/kg) (W/kg) B₃ ¹⁾ (T) B₈ ¹⁾ (T) 93/6279 49.20 1.89 0.06 Zr ˜ 0.80 1.062 0.0744 74.154 351.926 1.913 2.080 93/6284 49.35 1.90 0.43 Zr ˜ 1.00 1.264 0.0945 87.404 404.535 1.835 2.039 93/6285 49.35 1.89 0.44 Zr ˜ 1.40 1.456 1.813 2.015 with air flow correction from B₄₀ Mechanical measurements B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ R_(m) R_(p0.2) A_(L) E-Modulus □_(el) Batch (T) (T) (T) (T) (T) (MPa) (MPa) (%) (GPa) HV (□mm²/m) 93/6279 2.158 2.188 2.209 2.237 2.261 798 420 6.7-8.1 233 250 0.447 93/6284 2.129 2.164 2.185 2.210 2.234 843 465 6.6-7.7 240 261 0.448 93/6285 2.104 2.140 808 504 4.8-7.2 243 279 0.454

TABLE 26 Anneal: 4 h/800° C./H2/OK/  With air flow correction from B₄₀ Magnetic measurements p_(Fe) ²⁾ p_(Fe) ²⁾ Wt-% H_(c) p_(hyst)/f f = 400 Hz f = 1000 Hz B₃ ¹⁾ B₈ ¹⁾ Batch Co V Nb Zr Ta (A/cm) (J/kg) (W/kg) (W/kg) (T) (T) 93/6655 49.15 1.90 0.10 #0.86 x 1.640 0.1279 98.076 421.081 1.623 1.959 93/6661 49.70 1.91 x #0.77 #0.16 1.380 0.1042 83.840 367.657 1.684 1.983 Magnetic measurements Mechanical measurements B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ R_(m) R_(p0.2) A_(L) E-Modulus Batch (T) (T) (T) (T) (T) (MPa) (MPa) (%) (GPa) HV 93/6655 2.084 2.137 2.167 2.204 2.232 848-869 460-462 7.0-7.5 240-247 249-260 93/6661 2.099 2.153 2.177 2.208 2.229 910-936 441-447 8.7-9.1 241-249 244-254 p_(hyst)/f: static hysteresis losses at B = 2 T ¹⁾Induction B at a field H in A/cm, e.g. B₂₄ at H = 24 A/cm ²⁾p_(Fe) at B = 2 T

TABLE 27 Quenching Choice of experiments: Microstructural state Quenching Batch 3 h/880° C. 3 h/900° C. 3 h/920° C. 3 h/940° C. 3 h/950° C. conditions 93/7179 α α α α + a α + a 2 h/970° C./air 49.2 Co/0 V/ little α′ little α′ 0.16 Ta/0.77 Zr 93/7180 α + α′ α + α′ α + α′ α′ α′ 2 h/900° C./air 49.2 Co/3 V / 0.16 Ta/0.77 Zr 93/7181 α α α α + a little α + α′ at 2 h/970° C./air 49.2 Co/1 V/ α′ edge more 0.16 Ta/0.77 Zr α′ 93/7182 α α α + a little α + a α + a 2 h/800° C./air 35 Co/2 V/ α′ little α′ little α′ 0.16 Ta/0.77 Zr 93/7183 α α α α α + a little 2 h/800° C./air 27 Co/2 V/ α′ 0.16 Ta/0.77 Zr

TABLE 28 Anneal: 1 h/720° C./H2/OK/ Wt. % Magnetic measurements; with air flow correction from B₄₀ Density H_(c) B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ Batch Co V Ta Zr (g/cm³) (A/cm) (T) (T) (T) (T) (T) (T) (T) 93/7180 49.2 3 0.16 0.77 8.12  12.761 0.093 0.319 1.229 1.666 1.843 1.971 2.047 93/7181 49.2 1 0.16 0.77 8.12  5.842 0.160 1.435 1.954 2.048 2.126 2.205 2.258 93/7182 35   2 0.16 0.77 8.004 9.285 0.120 0.643 1.811 1.931 2.033 2.137 2.211 93/7183 27   2 0.16 0.77 7.990 9.248 0.077 0.589 1.661 1.785 1.892 2.039 2.171 93/7184 10   2 0.16 0.77 7.872 6.228 0.103 1.105 1.484 1.603 1.708 1.842 1.985 74/5517 49.3 2 0.18 0.75 8.12  5.905 0.184 1.189 1.812 1.940 2.033 2.114 2.158 99/5278 Mechanical measurements R_(m) R_(p0.2) A_(L) E-Modulus Batch (MPa) (MPa) (%) (GPa) HV 93/7180 1328-1389  998-1018 10.1-11.9 255-263 394-412 93/7181  955-1145 819-897  5.1-11.2 240-261 364-371 93/7182 1301-1323  994-1016 11.1-12.1 254-267 375-390 93/7183 898-930 791-826 6.9-9.4 234-247 281-293 93/7184 580-597 492-500 16.4-17.4 208-221 180-188 74/5517 1203-1286 779-819 10.5-14.3 247-265 333-356 99/5278 ¹⁾Induction B at a field H in A/cm, e.g. B₃ at H = 3 A/cm

TABLE 29 ρ_(el) ³⁾ p_(1 T) ^(50 Hz) p_(1.5 T) ^(50 Hz) p_(2 T) ^(50 Hz) p_(1 T) ^(400 Hz) p_(1.5 T) ^(400 Hz) p_(2 T) ^(400 Hz) p_(1 T) ^(1000 Hz) p_(1.5 T) ^(1000 Hz) p_(2 T) ^(1000 Hz) Batch (μΩm) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) 93/7180 0.733 11.83 24.51 48.73²⁾ 99.78 247.8 425.0 279.9 683.4 1166 93/7181 0.365 6.372 14.35 25.76 64.20 141.5 246.5 203.8 468.3  834.5 93/7182 0.477 12.31 24.09 37.09²⁾ 106.7 248.3 343.9 295.4 613.2 1040 93/7183 0.457 13.42 26.25 42.26²⁾ 124.3 222.6 383.6 335.2 723.3 1162 93/7184 0.437 11.47 21.19²⁾ 33.87²⁾ 102.6 205.2 326.3²⁾ 301.3 632.7  984.3²⁾ 74/5517 — 5.8 14.02 25.2 53.9 118.2 234.2 168.7 401.3  728.8 99/5278 ²⁾Form factor FF = 1.111 ± 1% not fulfilled ³⁾ρ_(el) calculated from the gradient m of the line in p/f (f)-Diagram at B = 2 T with m˜1/ρ_(el) and ρ_(el)(Vacoflux 50) = 0.44 μΩm p_(1 T) ^(50 Hz) = hysteresis losses at an Induction B = 1 T and a Frequency f = 50 Hz

TABLE 30 Anneal: 2 h/750° C./H2/OK/ Magnetic measurements; with air flow correction from B₄₀ Wt. % density H_(c) B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ Batch Co V Ta Zr (g/cm³) (A/cm) (T) (T) (T) (T) (T) (T) (T) 93/7180 49.2 3.0 0.16 0.77 8.12 6.396 0.188 0.823 1.546 1.754 1.911 2.043 2.144 93/7181 49.2 1.0 0.16 0.77 8.12 2.660 0.701 1.872 2.053 2.125 2.185 2.240 2.276 93/7182 35 2 0.16 0.77 8.004 6.459 0.118 1.090 1.833 1.950 2.055 2.159 2.222 93/7183 27 2 0.16 0.77 7.990 7.507 0.079 0.803 1.654 1.765 1.869 2.020 2.168 93/7184 10 2 0.16 0.77 7.872 4.728 0.162 1.222 1.498 1.599 1.691 1.816 1.964 74/5517 49.3 2 0.18 0.75 8.12 2.248 0.970 1.830 2.011 2.081 2.134 2.179 2.206 99/5278 Mechanical measurements R_(m) R_(p0.2) A_(L) E-Modulus Batch (MPa) (MPa) (%) (GPa) HV 93/7180  961-1231 678-728 6.6-12.1 250-260 316-344 93/7181 930-946 602-611 7.7-8.2  248-259 292-303 93/7182  985-1266 790-802 5.4-13.7 258-263 323-339 93/7183 832-847 625-637 8.9-11.9 237-246 258-264 93/7184 515-527 315-327 20.0-22.9  206-213 142-145 74/5517  941-1179 551-563 8.4-14.7 216-239 274-291 99/5278 ¹⁾Induction B at a field H in A/cm, e.g. B₃ at H = 3 A/cm

TABLE 31 ρ_(el) ³⁾ p_(1 T) ^(50 Hz) p_(1.5 T) ^(50 Hz) p_(2 T) ^(50 Hz) p_(1 T) ^(400 Hz) p_(1.5 T) ^(400 Hz) p_(2 T) ^(400 Hz) p_(1 T) ^(1000 Hz) p_(1.5 T) ^(1000 Hz) p_(2 T) ^(1000 Hz) Batch (μΩm) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) 93/7180 0.720 5.560 13.91 22.92²⁾ 49.35 126.7 208.0 152.3 385.1 628.1 93/7181 0.350 2.955 6.606 11.24 35.62 77.80²⁾ 143.9 132.2 305.0 586.3 93/7182 0.493 7.965 17.15 25.97²⁾ 73.44 155.7²⁾ 248.7 213.8 462.5 804.2 93/7183 0.468 11.42 21.51 34.37²⁾ 99.72 200.1 318.0 288.7 613.8 980.3 93/7184 0.428 8.934 17.60 26.20²⁾ 82.67 160.9 261.1²⁾ 261.2 547.6 865.2²⁾ 74/5517 — 2.4 5.59 9.9 27.1 56.25 109.1 98.0 230.5 413.0 99/5278 ²⁾Form factor FF = 1.111 ± 1% not fulfilled ³⁾ρ_(el) calculated from the gradient m of the line p/f (f)-Diagram at B = 2 T with m ˜1/ρ_(el) and ρ_(el)(Vacoflux 50) = 0.44 μΩm ρ_(1 T) ^(50 Hz) = hysteresis losses at an Induction B = 1 T and a Frequency f = 50 Hz

TABLE 32 Anneal: 4 h/840° C./H2/OK/ Magnetic measurements; with air flow correction from B₄₀ Wt-% density H_(c) B₃ ¹⁾ B₈ ¹⁾ B₁₆ ¹⁾ B₂₄ ¹⁾ B₄₀ ¹⁾ B₈₀ ¹⁾ B₁₆₀ ¹⁾ Batch Co V Ta Zr (g/cm³) (A/cm) (T) (T) (T) (T) (T) (T) (T) 93/7180 49.2 3.0 0.16 0.77 8.12 6.398 0.150 0.512 1.099 1.384 1.652 1.907 2.037 93/7181 49.2 1.0 0.16 0.77 8.12 1.396 1.614 1.958 2.104 2.165 2.213 2.254 2.282 93/7182 35 2 0.16 0.77 8.004 2.355 0.372 1.556 1.818 1.953 2.092 2.199 2.240 93/7183 27 2 0.16 0.77 7.990 3.357 0.154 1.399 1.620 1.717 1.820 1.974 2.141 93/7184 10 2 0.16 0.77 7.872 3.187 0.386 1.249 1.482 1.576 1.663 1.792 1.944 74/5517 49.3 2 0.18 0.75 8.12 1.065 1.618 1.942 2.074 2.131 2.165 2.196 2.216 99/5278 Mechanical measurements R_(m) R_(p0.2) A_(L) E-Modulus Batch (MPa) (MPa) (%) (GPa) HV 93/7180  995-1199 553-600  8.3-12.2 250-258 287-302 93/7181 662-736 379-387 5.3-6.2 257-259 220-233 93/7182 811-945 478-490 5.8-7.9 253-261 240-254 93/7183 701-730 379-390 10.8-12.7 236-246 202-217 93/7184 439-451 190-195 23.8-26.5 198-211 116-121 74/5517  841-1013 410-427  7.6-10.9 236-271 235-248 99/5278 ¹⁾Induction B at a field H in A/cm, e.g. B₃ at H = 3 A/cm

TABLE 33 ρ_(el) ³⁾ p_(1 T) ^(50 Hz) p_(1.5 T) ^(50 Hz) p_(2 T) ^(50 Hz) p_(1 T) ^(400 Hz) p_(1.5 T) ^(400 Hz) p_(2 T) ^(400 Hz) p_(1 T) ^(1000 Hz) p_(1.5 T) ^(1000 Hz) p_(2 T) ^(1000 Hz) Batch (μΩm) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) (W/kg) 93/7180 0.649 5.847 13.67 18.82²⁾ 53.17 121.7 179.0²⁾ 163.3 385.2 559.8 93/7181 0.316 1.829 3.883 6.266 26.64 61.00 104.5 108.6 272.9 510.6 93/7182 0.446 3.770 6.844 8.882²⁾ 40.08 68.84 118.0 139.1 263.8 464.9 93/7183 0.408 5.736 11.32 16.59²⁾ 56.00 119.3 175.4 182.5 409.4 635.5 93/7184 0.370 6.314 12.96²⁾ 19.54²⁾ 63.53 124.4 204.3²⁾ 205.4 486.0 707.4²⁾ 74/5517 — 1.7 3.348 5.4 21.6 46.85 78.5 82.4 183.8 352.5 99/5278 ²⁾factor FF = 1.111 ± 1% not fulfilled ³⁾ρel calculated from the gradient m of the straight line in p/f (f)-Diagram at B = 2 T with m ˜1/ρ_(el) and ρ_(el)(Vacoflux 50) = 0.44 μΩm ρ1 T^(50 Hz) = hysteresis losses at an induction B = 1 T and a Frequency f = 50 Hz 

1. A high-strength, soft-magnetic iron-cobalt-vanadium alloy, consisting of 35≦Co≦55% by weight, 0.75≦V≦2.5% by weight, 0≦(Ta+2×Nb)≦1% by weight, 0.3<Zr≦1.5% by weight, Ni≦5% by weight, remainder Fe and melting-related and/or incidental impurities.
 2. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the zirconium content is 0.5≦Zr≦1% by weight.
 3. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the zirconium content is 0.6≦Zr≦0.8% by weight.
 4. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the cobalt content is between 45≦Co≦50% by weight.
 5. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the cobalt content is between 48≦Co≦50% by weight.
 6. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the vanadium content is between 1≦V≦2% by weight.
 7. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the vanadium content is between 1.5≦V≦2% by weight.
 8. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the niobium and/or tantalum content is between 0.04≦(Ta+2×Nb)≦0.8% by weight.
 9. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the niobium and/or tantalum content is between 0.04≦(Ta+2×Nb)≦0.5% by weight.
 10. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, in which the niobium and/or tantalum content is between 0.04≦(Ta+2×Nb)≦0.3% by weight.
 11. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the nickel content is Ni≦1% by weight.
 12. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the nickel content is Ni≦0.5% by weight.
 13. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the content of melting-related and/or incidental metallic impurities is Cu≦0.2, Cr≦0.3, Mo≦0.3, Si≦0.5, Mn≦0.3 and Al≦0.3.
 14. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the content of melting-related and/or incidental metallic impurities is Cu≦0.1, Cr≦0.2, Mo≦0.2, Si≦0.2, Mn≦0.2 and Al≦0.2.
 15. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the content of melting-related and/or incidental metallic impurities is Cu≦0.06, Cr≦0.1, Mo≦0.1, Si≦0.1 and Mn≦0.1.
 16. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the content of melting-related and/or incidental nonmetallic impurities is P≦0.01, S≦0.02, N≦0.005, O≦0.05 and C≦0.05.
 17. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the content of melting-related and/or incidental nonmetallic impurities is P≦0.005, S≦0.01, N≦0.002, O≦0.02 and C≦0.02.
 18. The high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1, wherein the content of melting-related and/or incidental nonmetallic impurities is S≦0.005, N≦0.001, O≦0.01 and C≦0.01.
 19. The use of the high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1 as a material for magnetic bearings.
 20. The use of the high-strength, soft-magnetic iron-cobalt-vanadium alloy as claimed in claim 1 as a material for rotors.
 21. A high strength, soft-magnetic iron-cobalt-vanadium alloy, consisting of 45≦Co≦50% by weight, 1≦V≦2% by weight, 0.04≦(Ta+2×Nb)≦0.8% by weight, 0.5≦Zr≦1% by weight, Ni≦1% by weight, remainder Fe and melting-related and/or incidental impurities.
 22. The high strength, soft-magnetic iron-cobalt-vanadium alloy of claim 21, wherein the content of melting-related and/or incidental metallic impurities is: Cu≦0.2, Cr≦0.3, Mo≦0.3, Si≦0.5, Mu≦0.3, and Al≦0.3.
 23. A high strength, soft-magnetic iron-cobalt-vanadium alloy, consisting of: 48≦Co≦50% by weight, 1.5≦V≦2% by weight, 0.04≦(Ta+2×Nb)≦0.5% by weight, 0.6≦Zr≦0.8% by weight, Ni≦0.5% by weight, remainder Fe and melting-related and/or incidental impurities.
 24. The high strength, soft-magnetic iron-cobalt-vanadium alloy of claim 23, wherein the content of melting-related and/or incidental metallic impurities is: Cu≦0.1, Cr≦0.2, Mo≦0.2, Si≦0.2, Mu≦0.2 and Al≦0.2. 